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International Journal of Refractory Metals & Hard Materials 78 (2019) 247–253 Contents lists available at ScienceDirect International Journal of Refractory Metals & Hard Materials journal homepage: www.elsevier.com/locate/IJRMHM WC-Co-Re cemented carbides: Structure, properties and potential applications T ⁎ I. Konyashina,b, , S. Faraga, B. Riesa, B. Roebuckc a Element Six GmbH, Burghaun D-36151, Germany b National University of Science and Technology MISiS, Moscow 119049, Russia c National Physical Laboratory, Teddington TW11 0LW, United Kingdom ARTICLE INFO ABSTRACT Keywords: Cemented carbides of the WC-Co-Re system represent a new class of hard materials having a significantly in- Cemented carbides creased Young's modulus, hot hardness and high temperature creep resistance. The WC-Co-Re phase diagram Co-Re binders was evaluated and compared with the corresponding WC-Co phase diagram. Physical and mechanical properties Microstructure of such composites were measured at room and elevated temperatures and compared with those of conventional High-temperature properties WC-Co cemented carbides. Microstructures of the WC-Co-Re cemented carbides at different carbon contents, binder contents and WC grain sizes were examined. Rhenium being dissolved in the Co-based binder is found to be a very strong grain growth inhibitor with respect to WC coarsening during liquid-phase sintering. The Young's modulus, hot hardness and high temperature creep resistance of the WC-Co-Re cemented carbides are greater than those of conventional WC-Co cemented carbides. Due to their unique properties the WC-Co-Re materials can find applications in use in high-pressure high-temperature components for synthesis of diamond and c-BN and cutting Ni-based super alloys and other heat-generating workpiece materials. 1. Introduction resistance of the composite materials, which in turn is dependent on its Young's modulus and high-temperature creep resistance. It is well known that high-pressure high-temperature (HPHT) It is well understood that additions of Re to binders of WC-based components such as anvils and dies employed for the synthesis of dia- cemented carbides allows improvement of their high-temperature mond, polycrystalline diamond (PCD) or cubic boron nitride (c-BN) are properties [4–10]. subjected to harsh operation conditions. They include ultra-high pres- Cemented carbides containing rhenium were first patented in 1949 sures (above 5 GPa) and relatively high temperatures (of above [3]; however, at this time no information regarding potential ad- 1400 °C). Presently, there is a general trend to fabricate diamond and c- vantages of partial substitution of Co by Re in the cemented carbide BN by so-called direct conversion, which enables the synthesis of dia- binder for high temperature applications was available. mond or c-BN out of graphite or hexagonal boron nitride without em- WC-Co-Re cemented carbides characterized by particular Re to Co ploying catalysts [1,2]. As a result, nano-structured diamonds and c-BN ratios were developed for fabricating cutting tools in the Soviet Union with exceptionally high hardness values can be obtained. However, [4–8]. Although, it was established that such cemented carbides are direct conversion is only achievable at extremely higher pressures ex- characterized by significantly higher hot hardness and improved per- ceeding 12 GPa. Such unfavorable conditions inevitably lead to the formance at elevated temperatures in comparison with conventional deformation of HPHT components and, if the deformation exceeds a WC-Co materials, such composites were not applied in HPHT applica- certain level, the components fail. Currently, the large-scale fabrication tions. of superhard materials at pressures above 12 GPa is limited by rela- Cemented carbides containing Co-Re binders and mixed (W,Re)C tively short lives of HPHT components made of conventional WC-Co carbides were examined in refs. [9, 10]. It was found that rhenium materials. Therefore, the development and research of novel cemented added to the Co-based binder phase forms a solid solution with cobalt carbides with improved high temperature properties currently can be decreasing the stacking fault energy of the binder phase, which leads to considered as a topic of great interest. Prolonging the lifetime of HPHT the stabilization of the hcp Co modification. Tungsten and rhenium components can generally be achieved by improving the deformation were found to form mixed carbides having different compositions. ⁎ Corresponding author at: Element Six GmbH, Burghaun D-36151, Germany. E-mail address: [email protected] (I. Konyashin). https://doi.org/10.1016/j.ijrmhm.2018.10.001 Received 24 July 2018; Received in revised form 12 September 2018; Accepted 3 October 2018 Available online 05 October 2018 0263-4368/ © 2018 Elsevier Ltd. All rights reserved. I. Konyashin et al. International Journal of Refractory Metals & Hard Materials 78 (2019) 247–253 Waldorf et al. examined the performance of WC-Co-Re cemented carbides in machining Ni-based superalloys and established that their tool lifetime is prolonged by up to 150% in comparison with conven- tional WC-Co carbide grades [11]. The major objective of this work was to optimize fabrication con- ditions of WC-Co-Re cemented carbides, produce such cemented car- bides with different compositions and WC mean grain sizes, and ex- amine their physical and mechanical properties at room temperature and elevated temperatures. 2. Experimental procedure A number of laboratory batches of WC-Co-Re cemented carbides with different carbon contents, WC mean grain sizes, binder contents and ratios between Re and Co were produced and examined. WC powders with mean grain sizes of 3 μm and 0.8 μm, a Co powder with a grain size of about 1 μm and a Re powder with a grain size of 1–3 μm were milled in hexane with different amounts of carbon black and 1.8% paraffin wax by use of attritor-mills and ball-mills. The batches pro- duced from the medium-coarse WC powder with a mean particle size of 1.7 μm were designated as “medium-grain cemented carbides” and Fig. 1. Vertical sections of the W-Co-Re-C phase diagram (red lines) at 9 wt% those obtained from the fine-grain WC powder with a particle size of Re + 6 wt% Co in comparison with the W-Co-C phase diagram at 10 wt% Co 0.6 μm were designated as “submicron cemented carbides”. After (black lines). The WC-Co diagram is redrawn from Ref. [13]. (For interpretation of the references to color in this figure legend, the reader is referred to the web drying a slurry obtained in such a way, carbide samples were pressed version of this article.) and sintered in a laboratory Sinter-HIP furnace at a temperature of 1520 °C for 1 h followed by cooling at rates varying from 0.5 degrees/ min to 4 degrees/min. The Vickers hardness was measured according to above approx. 1430 °C. This means that if the WC-Co-Re cemented the ISO 3878 standard at a load of 300 N. The transverse rupture carbides with medium-low and low carbon contents are fast cooled η strength (TRS) was measured according to the ISO 3327 standard. The from sintering temperatures, they could contain -phase, which did not compression strength was measured according to the ISO 4506 standard decompose to the thermodynamically stable mixture of WC + Co/Re. at room and elevated temperatures. The hot hardness and length of the Therefore, after sintering WC-Co-Re cemented carbides have to be Palmqvist cracks were measured at a load of 300 N at temperatures of cooled down at relatively low rates to ensure a full decomposition of the η 300 °C, 500 °C and 800 °C in an Ar atmosphere. The Young's modulus -phase, which co-exists with WC and liquid phase at temperatures of was measured with the aid of the ultrasonic method by means of above 1420 °C. This is illustrated in Fig.2, which shows that the mi- measuring the transverse and longitudinal components of the speed of crostructure of the WC-Co-Re batch with a medium-low carbon content η η sound through the material. The high temperature creep resistance was comprises inclusions of -phase after fast cooling and is free of -phase examined at a temperature of 800 °C according to the procedure de- as a result of slow cooling. scribed in Ref. [12]. The XRD measurements were carried out on a The special features of the W-Co-Re-C phase diagram and the pre- Bruker D8 Advance instrument using a Co anode. sence of large amounts of Re dissolved in the binder of WC-Co-Re ce- mented carbides lead to some peculiarities of their microstructure and 3. Results and discussion properties. Figs. 3 and 4 show the typical microstructure of the medium-grain Fig. 1 schematically shows the W-Co-Re-C phase diagram at 9 wt% WC-Co-Re cemented carbide in comparison with that of a conventional Re + 6 wt% Co, which was elaborated based on the results obtained in WC-Co material obtained from the same grade of WC powder. As one the literature (Ref. [6]) and experimental results of the present work, in can see in Fig.3, the microstructure of the WC-Co-Re cemented carbide fi fi comparison with the corresponding WC-Co diagram at 10 wt% Co re- is signi cantly ner than that of the conventional WC-Co cemented drawn from Ref. [13]. When taking into account that Re has a sig- carbide. Therefore, Re acts as a strong WC grain growth inhibitor nificantly higher density than Co, the WC-Co Re cemented carbide with suppressing the WC coarsening process. According to the results of Ref. the binder containing 9 wt% Re and 6 wt% Co is characterized by nearly [14] Re segregates at WC/binder grain boundaries of WC-Co-Re ce- the same percentage of the binder phase by volume in comparison with mented carbides.

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